EP0164263A2 - Fabrication d'une tôle d'acier destinée au traitement de surface et exempte de lignes de Hartmann - Google Patents

Fabrication d'une tôle d'acier destinée au traitement de surface et exempte de lignes de Hartmann Download PDF

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Publication number
EP0164263A2
EP0164263A2 EP85303935A EP85303935A EP0164263A2 EP 0164263 A2 EP0164263 A2 EP 0164263A2 EP 85303935 A EP85303935 A EP 85303935A EP 85303935 A EP85303935 A EP 85303935A EP 0164263 A2 EP0164263 A2 EP 0164263A2
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EP
European Patent Office
Prior art keywords
steel sheet
rolling
steel
less
weight
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP85303935A
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German (de)
English (en)
Other versions
EP0164263B1 (fr
EP0164263A3 (en
Inventor
Takashi C/O Research Laboratories Obara
Kazunori C/O Research Laboratories Osawa
Minoru C/O Research Laboratories Nishida
Kei C/O Research Laboratories Sakata
Hideo C/O Chiba Works Kuguminato
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Steel Corp
Original Assignee
Kawasaki Steel Corp
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Publication date
Application filed by Kawasaki Steel Corp filed Critical Kawasaki Steel Corp
Publication of EP0164263A2 publication Critical patent/EP0164263A2/fr
Publication of EP0164263A3 publication Critical patent/EP0164263A3/en
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Publication of EP0164263B1 publication Critical patent/EP0164263B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0268—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment between cold rolling steps

Definitions

  • the present invention relates to the production of a base sheet to be surface-treated, that is, a steel sheet as a base steel sheet to be plated for a surface-treated sheet such as tinplate and tin free steel in which a steel sheet is thinly plated with Sn or Cr, and is to effectively avoid the occurrence of the stretcher strain in the treatment, particularly drawing, made on the surface-treated steel sheet.
  • the tempering degree is classified into several ranges from T-1(HR30T:49 ⁇ 3) to T-6(HR30T:70 ⁇ 3) depending upon intended Rockwell T hardnesses (HR30T).
  • Such classification is made with respect to the box annealing, and in particular the classification from the T-4-CA to T-6-CA (HR30T:61 ⁇ 3 to 70 ⁇ 3) is specified with respect to the continuous annealing.
  • the present invention is particularly suitable for the tinplate having the tempering degree of T2 or higher among the above-mentioned classification ranges and tin-free steel similar thereto.
  • the base steel sheet of T-1 to T-4 grades to be plated as tinplate there has been heretofore mainly used a low carbon aluminum-killed steel having 0.01 to 0.10% by weight (hereinafter also referred to briefly as "%" with respect to the other components of the steel), while as the base sheet of T-5 and T-6 grades, use has been principally made of a low carbon aluminum-killed steel in which P or N is added to increase the hardness.
  • the relation between the annealing method performed on the base steel sheet to be surface-treated and the properties of the tinplate is as follows: Box annealing: Since cooling is gradually performed down near room temperature in a few or several days after recrystallization (550-700°C), most of carbon in the steel precipitates as carbide. On the other hand, nitrogen in the steel precipitates as aluminum nitride during heating.
  • Continuous annealing After heating is carried out rapidly up to 600 to 730°C at 10-30°C/sec., and recrystallization is performed while the temperature is kept for several ten seconds, cooling is carried out down to room temperature at 5-50°C/sec. Accordingly, most of C and N exist in the solid-solution state. Consequently, the dislocation is introduced into the steel through temper rolling and solute C and N precipitated on the dislocation lines through plated tin-alloying treatment after the tin plating cause strain aging hardening. Thus, when this steel sheet is worked into a can or the like, "texture" pattern (called “stretcher strain”) caused by yield point elongation is formed to conspicuously deteriorate the outer appearance.
  • This publication discloses that aluminum-killed steel containing not more than 0.1% (not more than 0.04% in the below-mentioned Examples) of C, not more than 0.05% of Si, 0.05 to 0.4% of Mn, 0.01 to 0.1% of acid soluble AI, and 0.002 to 0.01% of N is used as a base material, hot rolling and the cold rolling are performed at a hot rolling finish temperature of from 700 to 900°C and at cold rolling reduction of 75-93%, respectively, followed by the continuous annealing to give a surface hardness of 43 to 58, and then wet type temper rolling is carried out at a rate of 1.5 to 35% depending upon a desired tempering degree in a range of HR30:44-75 of the surface hardness.
  • this method can attain the hardness as one of the material characteristics required in the tin plate, but it utterly failed to mention the countermeasure in the prevention of the stretcher strain produced in the processing.
  • the base sheet which is completely freed from the aging after baking can not be produced.
  • the strain aging takes place when alloying treatment is made at 230-300°C for a few seconds after the temper rolled steel sheet to be plated is plated with tin or when heating is done in drying to obtain the tin free steel after chromium galvanization is performed, so that a conspicuous stretcher strain is induced in processing such as plate working.
  • Japanese Patent application No. 5,425/1983 was filed with respect to a method of manufacturing the hard base steel sheet to be plated with tin which is free from the occurrence of the stretcher strain by continuously annealing an extremely low carbon steel sheet which contains not more than 0.0030% of C and a cold rolled steel sheet to which Nb or Ti is added upon necessity and temper rolling it at not less than 10%.
  • the object of the present invention is to provide a method of manufacturing a base steel sheet to be surface-treated while being able to advantageously restrain the stretcher strain in the processing.
  • the present inventors Upon having examined the method of manufacturing the tinplate being utterly free from the occurrence of the stretcher strain even after tin-melting treatment as well as baking treatment following the tin plating, the present inventors have found that even when the content of C is in a range of not more than 0.007% which can be relatively easily attained, the object intended by the present invention can be advantageously accomplished by performing temper rolling at a draft of not less than 7% by means of two or more stand rolling mill.
  • a method of manufacturing a base steel sheet which method comprises combined steps of: hot rolling a steel slab containing not more than 0.0070% by weight of C (hereinafter referred to briefly as "%" for simplification with respect to the contents of the steel components), not more than 0.1% of Si, not more than 0.5% of Mn, 0.010 to 0.080% of Al, not more than 0.0050% of N, not more than 0.030% of S provided that the ratio of Mn/S is not less than 10, and not more than 0.030% of P while the hot rolling being terminated at a finish temperature of not less than 800°C; cold rolling thus obtained hot rolled steel sheet in an ordinary manner; continuously annealing the cold rolled steel sheet in which heating is done up to a temperature from a recrystallization temperature to 800°C, followed by cooling; and then temper rolling the annealed steel sheet at a reduction of not less than 7% by using two or more stand rolling mill, whereby the thus obtained base sheet to
  • the behavior of the steel components of a base steel sheet to be surface-treated, particularly, C is important.
  • the content of C is conventionally as high as 0.01 to 0.10%, a large amount of exists in the solid-solution state in the steel due to the quenching during the continuous annealing, and the solute C precipitates on the dislocation lines in the temper rolling and plating-alloying treatment subsequent to the plating to cause the stretcher strain. Accordingly, it is preferable that the content of C present in the solid-solution state in the continuously annealed steel is as small as possible.
  • the most effective method of reducing the content of C in the solid-solution state is to reduce the content of C contained in the steel.
  • Each steel was forged to be a sheet bar having a thickness of 30 mm. Then, the hot rolling was performed to obtain a hot rolled sheet of 2.6 mm while the sheet bar was heated at 1,250°C and the finishing temperature was 860°C. Immediately thereafter, the hot rolled sheet was placed into a furnace of 560°C, and gradually cooled for 30 minutes, which corresponds to the treatment at a coiling temperature of 560°C.
  • the resulting steel sheet was cold rolled up to a thickness of 0.32 mm by a small scale rolling mill after pickling, and then subjected to the recrystallization annealing in the continuous annealing cycle.
  • the cold rolled steel sheet was rapidly heated up to 710°C at a rate of 15°C/sec. and maintained at this temperature for 30 minutes, and then quenched down to room temperature at a rate of 10°C/sec.
  • the baking treatment was carried out at 210°C for 20 minutes.
  • the steel sheet was drawn up to a depth of 5 mm with respect to a steel sheet piece punched in a diameter of 95 mm under the conditions that the diameter of a punching die was 50 mm, a blank holding force was 1 ton and the diameter of a punch was 33 mm.
  • the occurrence of the strain pattern in the drawing was observed by eyes.
  • the relation among the content of C, the temper rolling reduction and the stretcher strain is shown in Fig. 1.
  • Mn Since S which may cause brittleness at the hot rolling is required to be fixed in a form of MnS, Mn is necessary to be Mn/S ⁇ 10.
  • Al is necessary to fix N in a form of aluminum nitride, it is necessary that Al is in an amount of 0.010% at the minimum. The addition of too much amount thereof leads to cost-up, and thus the upper limit is set at 0.080%.
  • N may cause the stretcher strain in the processing of the product as in the case with C if N is present in the solid-solution state after the continuous annealing
  • N is preferably as few as possible.
  • the upper limit thereof is set at 0.0050%, the above-mentioned fixing with Al can be attained.
  • the slab having appropriately undergone the slabbing in the ingot making or more preferably the continuous casting is subjected to the hot rolling during the processing processes according to the present invention.
  • the hot rolling finish temperature is set at not lower than 800°C.
  • the other hot rolling conditions and cold rolling conditions than the above are not particularly required to be restricted, and may be according to the ordinary ones.
  • the annealing temperature In the conditions of the continuous annealing following the cold rolling, it is necessary to set the annealing temperature at not lower than the recrystallization temperature. However, if the annealing temperature exceeds 800°C, it becomes not only extremely difficult to pass the sheet in the continuous annealing but also the grain becomes larger to cause the rough surface. Thus, the upper- limit of the annealing temperature is set at 800°C.
  • the plated steel sheet such as the tinplate or tin free steel having the peculiarity that completely no stretcher strain caused by the yield point elongation, that is, the strain pattern, is produced after the tin plating and tin-melting treatment or the corresponding treatment in the tin free steel is obtained merely by employing the extremely low carbon aluminum-killed steel with not more than 0.0070% of C as a raw material and temper rolling of the cold rolled steel sheet thereof at 7% after the continuous annealing.
  • the steel sheet as continuous annealed is extremely soft, because the raw material is an extremely low carbon Al killed steel, and therefore, the rolling at 7% reduction can be easily performed by the temper rolling mill.
  • the steel sheet having undergone the continuous annealing was temper rolled at 7-20% in two passes and maintained in an oil bath at 250°C for 3 seconds, and then was subjected to a treatment corresponding to baking at 210°C for 20 minutes.
  • the present invention is to establish the process of advantageously producing the tinplate and the tin-free steel with the temper degree of not less than 2 which is free from the production of the stretcher strain on the basis of the completely novel concept that the extremely low carbon Al-killed steel containing not more than 0.0070% of C as the raw material is combined with the temper rolling.
  • Any sort of the conventionally used rolling mills having two or more stands may do.
  • a steel having a composition shown in Table 1 was prepared through melting in a converter to prepare a slab in continuous casting.
  • the slab was finished to be 2.3 mm under the hot rolling conditions shown in Table 1.
  • the resulting sheet was cold rolled down to 0.8 mm by means of a tandem rolling mill after pickling.
  • the steel sheet thus obtained was further subjected to a treatment corresponding to baking at 210°C for 20 minutes, and the hardness was measured, while shallow drawing test similarly as mentioned in the fundamental experiment was carried out thereon.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)
  • Arc Welding In General (AREA)
  • Seal Device For Vehicle (AREA)
  • Coating Apparatus (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
EP85303935A 1984-06-08 1985-06-04 Fabrication d'une tôle d'acier destinée au traitement de surface et exempte de lignes de Hartmann Expired - Lifetime EP0164263B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP59116612A JPS60262918A (ja) 1984-06-08 1984-06-08 ストレツチヤ−ストレインの発生しない表面処理原板の製造方法
JP116612/84 1984-06-08

Publications (3)

Publication Number Publication Date
EP0164263A2 true EP0164263A2 (fr) 1985-12-11
EP0164263A3 EP0164263A3 (en) 1987-01-21
EP0164263B1 EP0164263B1 (fr) 1990-12-12

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EP85303935A Expired - Lifetime EP0164263B1 (fr) 1984-06-08 1985-06-04 Fabrication d'une tôle d'acier destinée au traitement de surface et exempte de lignes de Hartmann

Country Status (10)

Country Link
US (1) US4586965A (fr)
EP (1) EP0164263B1 (fr)
JP (1) JPS60262918A (fr)
KR (1) KR900004405B1 (fr)
AU (1) AU557182B2 (fr)
CA (1) CA1241583A (fr)
DE (1) DE3580865D1 (fr)
ES (1) ES8604653A1 (fr)
NO (1) NO160496C (fr)
ZA (1) ZA854179B (fr)

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0556834A2 (fr) * 1992-02-21 1993-08-25 Kawasaki Steel Corporation Procédé de fabrication de tôles en acier à résistance élevée pour des boîtes
EP0565066A1 (fr) * 1992-04-06 1993-10-13 Kawasaki Steel Corporation Tôle noire ou fer blanc pour la production de boîtes et procédé de fabrication
WO1996026295A1 (fr) * 1995-02-24 1996-08-29 Sollac Procede d'elaboration d'une tole ou d'une bande en acier pour la realisation d'une boite et tole ou bande en acier obtenue par ce procede
EP1247871A3 (fr) * 2001-04-06 2004-01-21 ThyssenKrupp Stahl AG Méthod de fabrication d'un tôle noire ayant une ductilité élevée et utilisation d'un acier
US7501031B2 (en) * 2004-06-18 2009-03-10 Nippon Steel Corporation Steel sheet for tin plated steel sheet and tin-free steel sheet each having excellent formability and manufacturing method thereof
CN104988387A (zh) * 2015-06-19 2015-10-21 唐山不锈钢有限责任公司 Mrt-4镀锡板用热轧带钢的生产方法
CN108760524A (zh) * 2018-03-19 2018-11-06 江阴兴澄特种钢铁有限公司 一种降低含p热轧板卷曲中裂纹倾向的模拟试验方法

Families Citing this family (15)

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JPS6169928A (ja) * 1984-09-12 1986-04-10 Kawasaki Steel Corp 連続焼鈍によるしごき加工用鋼板の製造方法
JPS63134645A (ja) * 1986-11-26 1988-06-07 Nippon Steel Corp 伸びフランジ成形性の優れたｄｉ缶用鋼板
JPH079029B2 (ja) * 1988-06-17 1995-02-01 川崎製鉄株式会社 連続焼鈍設備における極薄硬質ぶりき原板の製造方法
US5156694A (en) * 1988-12-19 1992-10-20 Kawasaki Steel Corporation Method of producing formable thin steel sheets
US5053194A (en) * 1988-12-19 1991-10-01 Kawasaki Steel Corporation Formable thin steel sheets
AU721071B2 (en) † 1996-02-08 2000-06-22 Jfe Steel Corporation Steel sheet for 2 piece battery can having excellent formability, anti secondary work embrittlement and corrosion resistance
KR100338705B1 (ko) * 1997-07-18 2002-10-18 주식회사 포스코 용접성및내프루팅성이우수한가공용주석도금원판의제조방법
KR100350070B1 (ko) * 1997-12-29 2002-12-11 주식회사 포스코 단축공정에의한석도원판제조방법및장치
KR20020049920A (ko) * 2000-12-20 2002-06-26 이구택 에지부 표면결함이 없는 열연강판의 제조방법
KR20110126519A (ko) * 2008-12-19 2011-11-23 에누오케 가부시키가이샤 개스킷용 강판의 제조 방법 및 개스킷
JP5728856B2 (ja) * 2010-09-07 2015-06-03 Ｊｆｅスチール株式会社 部材の製造方法
CN102000696B (zh) * 2010-10-19 2013-02-13 无锡嘉联不锈钢有限公司 一种条纹不锈钢带的生产方法
CN102719731B (zh) * 2012-06-28 2016-03-02 宝山钢铁股份有限公司 二次冷轧荫罩带钢及其制造方法
KR101303657B1 (ko) * 2013-04-17 2013-09-04 그린산업(주) 방서와 전자파차폐를 위한 연철테이프 제조방법
CN103602884A (zh) * 2013-12-06 2014-02-26 马钢(集团)控股有限公司 一种超低碳铝镇静钢板及其生产方法

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US3260623A (en) * 1963-10-04 1966-07-12 American Can Co Method of tempering continuously annealed metal sheet
FR2260623A1 (fr) * 1974-02-09 1975-09-05 Nippon Steel Corp
JPS5597428A (en) * 1979-01-16 1980-07-24 Nippon Steel Corp Production of steel plate for easy open can with excellent can opening property and score processability
GB2081150A (en) * 1980-08-01 1982-02-17 Nippon Steel Corp Method of producing steel strip
EP0073092A1 (fr) * 1981-08-13 1983-03-02 Kawasaki Steel Corporation Procédé de fabrication de tôle noire à grade de dureté T-3
JPS58197224A (ja) * 1982-05-10 1983-11-16 Kawasaki Steel Corp 連続焼鈍による調質度ｔ↓１〜ｔ↓３を有する錫めっきあるいはティンフリー鋼板の製造方法
JPS59129733A (ja) * 1983-01-17 1984-07-26 Kawasaki Steel Corp ストレツチヤ−ストレインの発生しない硬質ぶりき用めつき原板の製造方法

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DE3166285D1 (en) * 1980-05-31 1984-10-31 Kawasaki Steel Co Method for producing cold rolled steel sheets having a noticeably excellent formability
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FR2260623A1 (fr) * 1974-02-09 1975-09-05 Nippon Steel Corp
JPS5597428A (en) * 1979-01-16 1980-07-24 Nippon Steel Corp Production of steel plate for easy open can with excellent can opening property and score processability
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JPS58197224A (ja) * 1982-05-10 1983-11-16 Kawasaki Steel Corp 連続焼鈍による調質度ｔ↓１〜ｔ↓３を有する錫めっきあるいはティンフリー鋼板の製造方法
JPS59129733A (ja) * 1983-01-17 1984-07-26 Kawasaki Steel Corp ストレツチヤ−ストレインの発生しない硬質ぶりき用めつき原板の製造方法

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PATENTS ABSTRACTS OF JAPAN, vol. 8, no. 251 (C-252)[1688], 16th November 1984; & JP-A-59 129 733 (KAWASAKI SEITETSU K.K.) 26-07-1984 *

Cited By (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0556834A2 (fr) * 1992-02-21 1993-08-25 Kawasaki Steel Corporation Procédé de fabrication de tôles en acier à résistance élevée pour des boîtes
EP0556834A3 (en) * 1992-02-21 1993-09-29 Kawasaki Steel Corporation Method of producing high-strength steel sheet used for can
EP0565066A1 (fr) * 1992-04-06 1993-10-13 Kawasaki Steel Corporation Tôle noire ou fer blanc pour la production de boîtes et procédé de fabrication
WO1996026295A1 (fr) * 1995-02-24 1996-08-29 Sollac Procede d'elaboration d'une tole ou d'une bande en acier pour la realisation d'une boite et tole ou bande en acier obtenue par ce procede
FR2730942A1 (fr) * 1995-02-24 1996-08-30 Lorraine Laminage Procede d'elaboration d'une tole ou d'une bande en acier pour la realisation d'une boite et tole ou bande en acier obtenue par ce procede
US6056832A (en) * 1995-02-24 2000-05-02 Sollac Method for producing a steel sheet or strip for making a can, and steel sheet or strip obtained by said process
EP1247871A3 (fr) * 2001-04-06 2004-01-21 ThyssenKrupp Stahl AG Méthod de fabrication d'un tôle noire ayant une ductilité élevée et utilisation d'un acier
US7501031B2 (en) * 2004-06-18 2009-03-10 Nippon Steel Corporation Steel sheet for tin plated steel sheet and tin-free steel sheet each having excellent formability and manufacturing method thereof
US8012276B2 (en) 2004-06-18 2011-09-06 Nippon Steel Corporation Method for manufacturing a steel sheet for tin plated steel sheet and tin-free steel sheet each having excellent formability
CN104988387A (zh) * 2015-06-19 2015-10-21 唐山不锈钢有限责任公司 Mrt-4镀锡板用热轧带钢的生产方法
CN104988387B (zh) * 2015-06-19 2017-04-12 唐山不锈钢有限责任公司 Mrt‑4镀锡板用热轧带钢的生产方法
CN108760524A (zh) * 2018-03-19 2018-11-06 江阴兴澄特种钢铁有限公司 一种降低含p热轧板卷曲中裂纹倾向的模拟试验方法

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US4586965A (en) 1986-05-06
EP0164263B1 (fr) 1990-12-12
AU4337185A (en) 1985-12-12
ZA854179B (en) 1986-01-29
NO160496C (no) 1989-04-26
KR860000396A (ko) 1986-01-28
JPS6330368B2 (fr) 1988-06-17
EP0164263A3 (en) 1987-01-21
ES8604653A1 (es) 1986-02-01
KR900004405B1 (ko) 1990-06-25
NO160496B (no) 1989-01-16
ES544004A0 (es) 1986-02-01
CA1241583A (fr) 1988-09-06
JPS60262918A (ja) 1985-12-26
DE3580865D1 (de) 1991-01-24
NO852140L (no) 1985-12-09
AU557182B2 (en) 1986-12-11

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